US9074271B2 - Dual-phase stainless steel sheet and steel strip and method of production - Google Patents

Dual-phase stainless steel sheet and steel strip and method of production Download PDF

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US9074271B2
US9074271B2 US13/637,690 US201113637690A US9074271B2 US 9074271 B2 US9074271 B2 US 9074271B2 US 201113637690 A US201113637690 A US 201113637690A US 9074271 B2 US9074271 B2 US 9074271B2
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dual
stainless steel
steel
martensite
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Shinichi Teraoka
Shunji Sakamoto
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0242—Flattening; Dressing; Flexing
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation

Definitions

  • the present invention relates to stainless steel which is excellent in corrosion resistance and abrasion resistance and which has little drop in mirror surface gloss or image reflectability of the surface even with long term use.
  • it is provided as the material for various parts such as reflectors of solar light and home lightening equipment, mirrors, machinery, and electrical and electronic equipment.
  • martensitic stainless steel As metal materials which are excellent in corrosion resistance and abrasion resistance, martensitic stainless steel, work hardening type austenitic stainless steel, precipitation hardening type and other stainless steel, and ferrite and martensite dual-phase structure stainless steel are known.
  • Martensitic stainless steel is made a martensite structure by quenching, so can be used while made a high strength. In most cases, it is quenched, then tempered.
  • the hardness is adjusted by the contents of C and N, the quenching conditions (solution heat treatment temperature, time, and cooling rate), and the tempering conditions (temperature and time).
  • Martensitic stainless steel is high in strength and low in toughness, so reduction of the surface roughness by temper rolling is not easy.
  • the steel is quenched from the austenite single-phase region to obtain a martensite single-phase structure.
  • Cr, Mo, and other elements which improve the corrosion resistance narrow the austenite single-phase formation temperature region, so the amounts of addition are limited.
  • SUS420J1 steel the amount of Cr is defined as 12 to 14%. For this reason, SUS420J1 steel generally only has the minimum extent of corrosion resistance as stainless steel.
  • SUS429J1 and SUS431 contain 15.00 to 17.00% of Cr. If these are made martensite single-phase structures, the ductility becomes low, while if they are made a ferrite or austenite phase and martensite dual-phase structure, the corrosion resistance is impaired.
  • SUS301 As a representative type of work hardening type austenitic stainless steel, SUS301 may be mentioned.
  • SUS301 has an austenite structure at the time of solution treatment. Due to the temper rolling after that, it gradually transforms to the work-induced martensite. Due to the increase in the rolling reduction, the work hardening of the two phases further progresses to make the strength higher.
  • composition of SUS301 is 17% Cr ⁇ 7% Ni. Expensive Ni in 7% is required, so the material cost becomes higher.
  • the amount of deformation martensite is affected by the material temperature at the time of cold rolling, so in general reverse type rolling in cold rolling of stainless steel, near the coil top and bottom where the rolling speed changes, a change occurs in the amount of deformation martensite and the change in hardness becomes large.
  • SUS301 is large in work hardening, so when cold rolling hot rolled sheet to finish it to the desired thickness, the rolling load force is high. Depending on the cold rolling speed, annealing process will become necessary and the productivity will otherwise become inferior.
  • SUS630 17Cr ⁇ 4Ni ⁇ 4Cu
  • 631 17Cr ⁇ 7Ni ⁇ 1.2Al
  • other martensite type precipitation hardened steel are the mainstream.
  • Martensite type precipitation hardened steel is obtained by solution heat treatment, then cooling to room temperature in the process of which making a martensite structure, then aging so as to cause the formation of precipitated phases rich in Cu and cause fine dispersed precipitation of the intermetallic worked NiAl compound and harden the steel.
  • Martensite type precipitation hardened steel also requires large amounts of expensive Ni, Cu, and other alloy elements so is high in material cost and is an expensive material.
  • Dual-phase structure stainless steel is obtained by cold rolling hot rolled steel sheet of a ferrite and carbonitride structure, then applying dual-phase annealing which heats this to the ferrite and austenite dual-phase region and cools it so as to transform the austenite phase to martensite and obtain a ferrite and martensite dual-phase structure at room temperature and, furthermore, applying temper rolling and aging.
  • Dual-phase structure stainless steel is developed based on compositions similar to SUS431 and SUS429J1.
  • the chemical compositions are suitably adjusted to adjust the amount of martensite in accordance with the required hardness.
  • Dual-phase structure stainless steel reportedly is high in strength and large in ductility, has small in-plane fluctuations in strength, and is excellent in shape flatness as features.
  • a representative ferritic stainless steel that is, SUS430 steel, is also reported to easily become a ferrite and martensite dual-phase structure by heating to the dual-phase region and cooling.
  • dual-phase structure stainless steel has a lower amount of Cr in the martensite phase than the ferrite phase, so a difference arises between the phases in the corrosion resistance and the corrosion resistance which is obtained in the average composition cannot be sufficiently obtained or the aging due to corrosion will differ between the phases and thereby unevenness of gloss or hue will occur and the beautiful appearance will be impaired.
  • the present invention was made to solve such a problem and has as its object to provide stainless steel which particularly improves the corrosion resistance of the martensite phase, achieves a corrosion resistance corresponding to 18 to 19Cr steel by a 17Cr base, withstands severe outdoor corrosion and abrasive environments, is free from reduction of long term performance as a mirror surface, is inexpensive, and is high in strength.
  • the inventors engaged in various studies on the method of improving the corrosion resistance in stainless steel which is based on 15 to 17Cr steel and has a ferrite and martensite dual-phase structure.
  • Dual-phase structure stainless steel which has a ferrite and martensite dual-phase structure differs in amount of Cr at the ferrite phase and the austenite phase at the time of dual-phase forming heat treatment, so usually the corrosion resistance of the martensite phase, which is obtained by transformation of the low Cr austenite phase, becomes lower than the ferrite phase and the corrosion resistance falls to less than the corrosion resistance corresponding to the amount of Cr of the average composition of the base material.
  • the Sn concentrates at the ferrite phase in the same way as Cr and Mo.
  • the martensite phase is improved more in corrosion resistance as an effect by Sn than the ferrite phase.
  • the Sn makes up for the difference of Cr and improves the corrosion resistance whereby at least a corrosion resistance corresponding to the amount of Cr of the average composition of the dual-phase structure is obtained.
  • the present invention was made based on the above discovery and has as its gist the following:
  • ⁇ p 420C+470N+23Ni+7Mn+9Cu ⁇ 11.5Cr ⁇ 11.5Si ⁇ 12Mo ⁇ 7Sn ⁇ 49Ti ⁇ 47Nb ⁇ 52Al+189 (a)
  • FIG. 1 is a view which shows the effect of addition of Sn on the corrosion resistance in ferrite structure stainless steel and dual-phase structure stainless steel.
  • C is an austenite stabilizing element and is particularly effective for strengthening the martensite by solid solution hardening.
  • the undissolved carbides at the time of solution treatment have the effects of strengthening the martensite and raising the abrasion resistance. These effects become remarkable when the content of C becomes 0.02% or more.
  • the content of C is made 0.20% or less.
  • the preferable content of C is 0.10 to 0.15%.
  • Si is a ferrite stabilizing element. It is large in solid solution hardening ability and causes the ferrite and martensite phases to harden. Further, in the steelmaking process, it also acts as a deoxidizing element. This action appears conspicuously when the content of Si is 0.10% or more. However, if the content of Si is over 1.0%, the phase balance suitable for dual-phase structure stainless steel can no longer be maintained.
  • the preferable content of Si is 0.20 to 0.70%.
  • Mn is an austenite stabilizing element and is an alloy element which is required for obtaining a more suitable phase balance of austenite and ferrite at the time of dual-phase forming annealing, so is included in 0.20% or more.
  • the austenite stabilizing ability of Mn is about half that of Ni, but this is an element which is cheaper than Ni.
  • the effect of lowering the Ms point is greater than Ni. Residual ⁇ is formed and the hardness falls.
  • Mn is an element which obstructs oxidation resistance. The surface quality sometimes falls due to the oxidation at the time of annealing. Accordingly, as a range with little effect in impairing quality, the content of Mn is made 2.0% or less.
  • the preferable content of Mn is 0.50 to 1.0%.
  • P is an element with a large solid solution hardening ability, but is a ferrite stabilizing element. Further, it is an element which is harmful to the corrosion resistance and toughness.
  • the ferrochrome material of stainless steel contains this as an impurity, but there is no technique for removing P from a melt of stainless steel, so the purity and amount of the ferrochrome material used determines the amount of P.
  • low P ferrochrome is expensive, so as the range not greatly degrading the material quality or corrosion resistance, the content of P is made 0.040% or less.
  • the preferable content of P is 0.030% or less.
  • S forms sulfide inclusions and degrades the usual corrosion resistance of steel materials (general corrosion resistance and pitting resistance), so the content has to be made 0.010% or less.
  • the preferable content of S is 0.003 to 0.008%.
  • Cr is an element which is effective for improving the usual corrosion resistance (general corrosion resistance and pitting resistance), but if the content is less than 15%, obtaining a sufficient corrosion resistance is difficult.
  • Cr is a ferrite phase ( ⁇ -phase) stabilizing element. If the content is over 18%, the stability of the austenite phase ( ⁇ -phase) falls and obtaining a high strength by forming a dual-phase structure becomes difficult.
  • the preferable content of Cr is 15.5 to 17.5%.
  • Ni is an austenite phase stabilizing element and greatly affects the austenite phase percentage at the time dual-phase forming annealing. To obtain a suitable phase percentage, an amount of Ni corresponding to the amount of Cr is necessary, so the content is made 0.5% or more. Ni is an expensive element. Excessive addition increases the alloy cost, so the content is made 2.5% or less. The preferable content of Ni is 1.0 to 2.0%.
  • Sn is a ferrite phase stabilizing element and an element which is effective for improving the corrosion resistance of the martensite phase.
  • Sn concentrates at the ferrite phase at the time of dual-phase forming annealing in the same way as Cr, but in a ferrite and martensite dual-phase structure, improves the corrosion resistance of the martensite phase as if compensating for the difference in the amount of Cr, so a corrosion resistance of at least the level corresponding to the amount of Cr of the average composition of the dual-phase structure is obtained.
  • the content of Sn is made 0.05% or more. Even if adding Sn in over 0.30%, the effect of improvement of the corrosion resistance of the martensite phase by the Sn becomes saturated and the alloying cost is needlessly increased, so the content is made 0.30% or less.
  • the preferable content of Sn is 0.1 to 0.25%.
  • N is an austenite stabilizing element and an element which is effective for strengthening the martensite, so the content is made 0.010% or more. Solute N acts to strengthen the passivation film or improve the corrosion resistance by suppressing sensitization. If excessively adding N, this causes gas porosity type defects, so the content is made 0.10% or less.
  • the preferable content of N is 0.02 to 0.06%.
  • B, Cu, Mo, and Al may be added.
  • B has the effect of preventing edge cracks due to the difference in deformation resistance between the ferrite phase and the austenite phase in the hot rolling temperature region, so the content when added is made 0.0003% or more. If the content of B is over 0.0050%, a drop in corrosion resistance due to precipitation of borides or a drop in the hot workability occurs, so the content is made 0.0050% or less. The preferable content of B is 0.0005 to 0.0030%.
  • Cu is an austenite stabilizing element and an alloy element which is effective for obtaining a phase balance of austenite and ferrite at the time of dual-phase forming annealing, so is added in accordance with need.
  • the content in the case of addition is 0.3% or more.
  • the austenite stabilizing ability of Cu is about half that of Ni, but this is an element which is cheaper than Ni.
  • the preferable content of Cu is 0.5 to 1.5%.
  • Mo is an element which has an effect of improving the corrosion resistance greater than Cr and is added in accordance with need.
  • the content when added is made 0.3% or more.
  • Mo like Cr, concentrates at the ferrite and the time of dual-phase forming annealing and expands the difference in corrosion resistance between the ferrite and martensite. Further, it is an expensive element and causes a rise in the manufacturing cost, so the content is made 2.0% or less.
  • the preferable content of Mo is 0.5 to 1.2%.
  • Al is an additional ingredient which is effective as a deoxidizing agent. To obtain the deoxidizing effect, the content is made 0.01% or more. If including Al in a large amount, cluster-shaped high melting point oxides are formed and cause surface defects of the slab. Furthermore, the weldability also becomes poorer, so the content is made 0.1% or less.
  • the preferable content of Al is 0.02 to 0.05%.
  • impurities which are unavoidably contained in stainless steel there are Nb, Ti, V, Ca, Mg, REM, Co, Y, Zr, etc. These elements enter from the slag in the refining process or the alloy materials and are not deliberately added.
  • the unavoidably contained amounts are 0.01% or less or so.
  • V is greater in unavoidably contained amount than other elements, that is, 0.05% or less.
  • the ⁇ p which is expressed by the following formula (a) is an indicator which expresses the maximum amount of the austenite phase in the dual-phase region of the ferrite phase and austenite phase of 1000 to 1150° C. and broadly matches the value expressed by the volume percentage % of the austenite phase.
  • ⁇ p 420C+470N+23Ni+7Mn+9Cu ⁇ 11.5Cr ⁇ 11.5Si ⁇ 12Mo ⁇ 7Sn ⁇ 49Ti ⁇ 47Nb ⁇ 52Al+189 (a)
  • ⁇ p is less than 60, the ferrite and martensite dual-phase structure will not become a sufficient hardness. Furthermore, if ⁇ p is 20 to 60, the hot workability at the time of hot rolling will fall and edge cracks will sometimes occur.
  • the characterizing feature of the present invention is the point of addition of Sn to dual-phase structure stainless steel. This effect will be explained below based on experimental findings.
  • a melt basically comprised of SUS430LX steel while as a representative example of a dual-phase structure, a melt basically comprised of 0.10C ⁇ 0.5Si ⁇ 0.35Mn ⁇ 17.1Cr ⁇ 1Ni ⁇ 0.03Nsteel, were smelted in a vacuum melting furnace. These were cast while changing the amount of Sn in the range of 0 to 0.30%.
  • the steel ingots were ground smooth at their surfaces, then were hot rolled to obtain thickness 3.0 mm hot rolled steel strips.
  • FIG. 1 shows the relationship between the amount of addition of Sn and the pitting potential when making the pitting potential of a test material not containing Sn “1” (pitting potential ratio).
  • the corrosion resistance of the martensite phase is inferior to the ferrite phase, so in the region where the amount of addition of Sn is small, the corrosion resistance is governed by the corrosion resistance of the martensite phase.
  • the martensite phase is improved more in corrosion resistance by the Sn than the ferrite phase, so if the amount of addition of Sn becomes greater, due to the effect of this, it is believed that the pitting potential rapidly rises.
  • the hardness is mainly governed by the amount of martensite, amount of solute carbon and nitrogen, tempering conditions, etc. and corresponds to the dislocation density.
  • the improvement in the corrosion resistance of the martensite phase due to the addition of Sn appears under a high dislocation density.
  • the Vicker's hardness is prescribed as being 200 HV or more.
  • the cooling rate at the time of martensite transformation is preferably made 20° C./s within the range of the composition and ⁇ p prescribed by the present invention as explained later.
  • stainless steel prepared to the above chemical composition is processed by ordinary methods by the steps of hot rolling, annealing of the hot rolled sheet, pickling, and cold rolling to obtain cold rolled stainless steel sheet (hereinafter referred to as “cold rolled steel sheet”) or cold rolled stainless steel strip (hereinafter referred to as “cold rolled steel strip”).
  • the heating temperature at the hot rolling is preferably 1140 to 1240° C. so as to secure the hot workability and prevent edge cracks of the end faces of the hot rolled sheet.
  • the coiling temperature is preferably 600 to 800° C. for softening the hot rolled sheet.
  • the hot rolled sheet is annealed so as to soften the hot rolled sheet before cold rolling.
  • a box-type annealing furnace is preferably used to perform this under conditions where it is held at 750 to 880° C. for 1 hour to 20 hours.
  • the cold rolling reduction is preferably made 60 to 80%.
  • the cold rolled steel sheet or cold rolled steel strip is run through a continuous annealing furnace where it is heated to the ferrite and austenite dual-phase region.
  • the heating temperature at this time is Ac1 or more. It has to be a temperature at which the ferrite recrystallizes, so it is made 850° C. or more.
  • the heating temperature affects the amount of austenite.
  • the amount of austenite greatly changes, so from the viewpoints of uniformity of structure and stability of material quality, 850° C. or more is preferable.
  • stainless steel which has a ferrite and austenite dual-phase structure is susceptible to creep deformation at a high temperature and easily elongates and is reduced in width in the running direction due to the running tension at the time of continuous heating. Creep deformation occurs more easily the higher the temperature, so the heating temperature is made not more than 1100° C.
  • the critical cooling speed which is required for martensite transformation of dual-phase structure stainless steel is slower than the cooling speed which is required for suppressing sensitization, so the cooling speed is preferably at least the 20° C./s which is required for preventing sensitization. Cooling from the heating temperature to 550° C. or less is preferable.
  • the steel strip made a ferrite and martensite dual-phase structure was temper rolled and aged in accordance with need.
  • Temper rolling is aimed at strengthening the ferrite phase compared with the martensite, while the aging is aimed at improving the toughness of the martensite.
  • the temper rolling rate has to be at least 10% for strengthening the ferrite phase. If cold rolling a dual-phase structure material which already has high strength down to a high rolling reduction, the productivity becomes poor and edge cracks of the width ends sometimes occurs, so the temper rolling rate is preferably 50% or less.
  • the aging temperature is preferably at least 300° C. where aging becomes possible by continuous annealing. 550° C. or less is preferable from the viewpoint of suppressing sensitization at the time of annealing.
  • cold rolling was used to form thickness 0.5 mm cold rolled steel strips.
  • the cold rolled steel strips were processed by dual-phase forming annealing by a continuous annealing furnace and temper rolling under the conditions which are shown in Tables 3 and 4, then part of the strips were aged.
  • the steels A1 to A31 of Table 1 are stainless steels which satisfy the composition prescribed in the present invention, while the steels a32 to a52 of Table 2 are comparative examples.
  • the steel a49 corresponds to SUS410, the steel a50 to SUS429J1, the steel a51 to SUS430, and the steel a52 to SUS431.
  • the obtained steel sheets were evaluated as follows:
  • the hardness was measured by the test method of Vicker's hardness prescribed in JIS 22244 and was measured from the surface of the steel sheet.
  • the amount of ferrite was identified by corrosively etching the structure by the Murakami reagent described in the Stainless Steel Handbook (issued 1976, 4th edition, p. 871), then combining microscopic observation and image analysis.
  • the corrosion resistance was evaluated by using the pitting potential measurement method of stainless steel prescribed in JIS G0577 and judging samples exhibiting a value the same or higher than SUS430LX steel as “good (+)” and samples exhibiting a lower value as “poor ( ⁇ )”.
  • the weather resistance was evaluated by testing a test piece which was polished to a mirror surface by a test repeating for six cycles a one-month exposure test outdoors and an abrasion test of plastic prescribed in JIS K7205 and evaluating the degree of deterioration of the mirror surface gloss.
  • the mirror surface glossiness was measured by the method 5 (GS20°) of the methods of measurement of mirror surface glossiness prescribed in JIS 28741. Samples where, as a result of measurement of the mirror surface glossiness, the drop in gloss was a small one of less than 50 were judged as “good (+)” and samples where a drop in gloss over 50 occurred were judged as “poor ( ⁇ )”.
  • edge cracks of a hot rolled sheet were evaluated by observing the hot rolled coil from the end faces, measuring the number of edge cracks, and ranking sheets with less than 0.25/km as “A”, 0.25/km to less than 1.25/km as “B”, 1.25/km to less than 2.5/km as “C”, and 2.5/km or more as “D”.
  • the steels A16 and A17 with B added had extremely little edge cracks at the width ends of the hot rolled sheets and exhibited excellent end face properties.
  • the steels a39 and a46 with a ⁇ p of less than 60 were good in corrosion resistance, but deteriorated upon abrasion and were poor in weather resistance.
  • the steel a32 with a C of less than 0.020 the steel a39 with a Cr of over 18%, an Sn of 0%, and a hardness of less than 200 HV was poor in corrosion resistance, further deteriorated upon abrasion, and was poor in weather resistance.
  • the steel a35 had an Mn of over 2%, so uneven gloss occurred at the time of dual-phase forming annealing and the result was poor.
  • the steel a41 had an Ni of over 2.5%, so the result was unsuitable in terms of costs as well.
  • the steel a44 had an N of over 0.09%, so gas porosity type defects appeared at the surface and the result was poor.
  • the steel a47 had an Al of over 0.1%, so inclusion type defects occurred and the result was poor.
  • cold rolling was used to form thickness 0.5 mm cold rolled steel strips.
  • the cold rolled steel strips were processed by dual-phase forming annealing by a continuous annealing furnace and temper rolling under the conditions which are shown in Tables 9 and 10, then part of the strips were aged.
  • the steels B1 to B31 of Table 7 are stainless steels which satisfy the composition which is prescribed in the present invention, while the steels b32 to b52 of Table 8 are comparative examples.
  • the steel b49 corresponds to SUS410, the steel b50 to SUS429J1, the steel b51 to SUS430, and the steel b52 to SUS431.
  • the steels b32 to b34, b39, b40, b42, and b44 to b52 with amounts of addition of Sn of less than 0.05%, the steels b38 and b49 with a Cr of less than 15%, the steel B37 with an S of over 0.01, the steel b36 with a P of over 0.04%, and the steel b43 with a B of over 0.0050% were poor in corrosion resistance.
  • the steels b39 and b46 with a ⁇ p of less than 60 were good in corrosion resistance, but deteriorated due to abrasion and were poor in weather resistance.
  • the steel b32 with a C of less than 0.020% and an Sn of 0% and the steel b39 with a Cr of over 18%, an Sn of 0%, and a hardness of less than 200 HV were poor in corrosion resistance, deteriorated due to abrasion, and were poor in weather resistance.
  • the steels b33, b41, b49, b50, and b52 with a ⁇ p of over 95 or a C of over 0.20% and the steel b45 with a Cu of over 2% were too hard and were poor in material quality.
  • the steel b35 had an Mn of over 2% and suffered from uneven gloss at the time of dual-phase forming annealing, so the result was poor.
  • the steel b41 had an Ni of over 2.5%, so was also unsuitable in terms of cost.
  • the steel b44 had an N of over 0.09%, gas porosity type defects appeared at the surface, and the result was poor.
  • the steel b47 had an Al of over 0.1%, so defects occurred due to inclusions and the result was poor.
  • the present invention it is possible to inexpensively provide high strength, dual-phase structure stainless steel which is improved in corrosion resistance of particularly the martensite phase, achieves a corrosion resistance corresponding to 18 to 19Cr steel based on 17Cr without changing the phase balance, withstands severe outdoor corrosion and abrasive environments, and does not drop in mirror surface gloss over a long term and possible to apply this as the material for various parts such as reflectors of solar light and home lightening equipment, mirrors, machinery, and electrical and electronic equipment, so the applicability in industry is large.

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US20170253945A1 (en) * 2014-09-17 2017-09-07 Nippon Steel & Sumikin Stainless Steel Corporation Martensitic stainless steel for brake disk and method for producing said steel
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Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS637338A (ja) 1986-06-27 1988-01-13 Nisshin Steel Co Ltd 面内異方性の小さい高延性高強度の複相組織クロムステンレス鋼板または鋼帯の製造法
JPS63169330A (ja) 1987-01-03 1988-07-13 Nisshin Steel Co Ltd 延性に優れた高強度複相組織クロムステンレス鋼帯の製造法
JPH07138704A (ja) 1993-11-12 1995-05-30 Nisshin Steel Co Ltd 高強度高延性複相組織ステンレス鋼およびその製造方法
JPH08319519A (ja) 1995-05-24 1996-12-03 Nisshin Steel Co Ltd 高強度複相組織ステンレス鋼帯又は鋼板の製造方法
JPH09263912A (ja) 1996-03-29 1997-10-07 Nisshin Steel Co Ltd 打抜き加工用高強度複相組織クロムステンレス鋼板およびその製造方法
JP2001288543A (ja) 2000-04-04 2001-10-19 Nippon Steel Corp 表面特性及び耐食性に優れたフェライト系ステンレス鋼及びその製造方法
JP2002105601A (ja) 2000-09-27 2002-04-10 Nisshin Steel Co Ltd 高強度複相ステンレス鋼及びその製造方法
JP2003328083A (ja) 2002-05-10 2003-11-19 Nisshin Steel Co Ltd 溶接構造物用高強度複相ステンレス鋼板およびその製造法
US20050173031A1 (en) 2004-01-29 2005-08-11 Jfe Steel Corporation High strength steel sheet and method for manufacturing same

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0463912A (ja) * 1990-07-02 1992-02-28 Sakae Nakao 内燃機関の吸気圧縮装置
US5843246A (en) * 1996-01-16 1998-12-01 Allegheny Ludlum Corporation Process for producing dual phase ferritic stainless steel strip
JP4524850B2 (ja) * 2000-04-27 2010-08-18 Ｊｆｅスチール株式会社 延性および歪時効硬化特性に優れた高張力冷延鋼板および高張力冷延鋼板の製造方法
IT1316030B1 (it) * 2000-12-18 2003-03-26 Acciai Speciali Terni Spa Procedimento per la fabbricazione di lamierini a grano orientato.
CA2777715C (en) * 2006-05-09 2014-06-03 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel excellent in resistance to crevice corrosion
CN101121995A (zh) * 2007-09-06 2008-02-13 朱育民 新马氏体系不锈钢材料及其制备方法和应用
KR101767017B1 (ko) * 2008-03-26 2017-08-09 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 용접 열 영향부의 내식성과 인성이 양호한 저합금 2상 스테인리스강

Patent Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS637338A (ja) 1986-06-27 1988-01-13 Nisshin Steel Co Ltd 面内異方性の小さい高延性高強度の複相組織クロムステンレス鋼板または鋼帯の製造法
JPS63169330A (ja) 1987-01-03 1988-07-13 Nisshin Steel Co Ltd 延性に優れた高強度複相組織クロムステンレス鋼帯の製造法
JPH07138704A (ja) 1993-11-12 1995-05-30 Nisshin Steel Co Ltd 高強度高延性複相組織ステンレス鋼およびその製造方法
US5624504A (en) 1993-11-12 1997-04-29 Nisshin Steel Co., Ltd. Duplex structure stainless steel having high strength and elongation and a process for producing the steel
JPH08319519A (ja) 1995-05-24 1996-12-03 Nisshin Steel Co Ltd 高強度複相組織ステンレス鋼帯又は鋼板の製造方法
JPH09263912A (ja) 1996-03-29 1997-10-07 Nisshin Steel Co Ltd 打抜き加工用高強度複相組織クロムステンレス鋼板およびその製造方法
JP2001288543A (ja) 2000-04-04 2001-10-19 Nippon Steel Corp 表面特性及び耐食性に優れたフェライト系ステンレス鋼及びその製造方法
JP2002105601A (ja) 2000-09-27 2002-04-10 Nisshin Steel Co Ltd 高強度複相ステンレス鋼及びその製造方法
JP2003328083A (ja) 2002-05-10 2003-11-19 Nisshin Steel Co Ltd 溶接構造物用高強度複相ステンレス鋼板およびその製造法
US20050173031A1 (en) 2004-01-29 2005-08-11 Jfe Steel Corporation High strength steel sheet and method for manufacturing same
TW200530409A (en) 2004-01-29 2005-09-16 Jfe Steel Corp High strength steel sheet and method for manufacturing same

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
International Search Report dated Jun. 28, 2011, issued in corresponding PCT Application No. PCT/JP2011/058483.
Machine-English translation of Japanese patent 07-138704, Miyakusu Katsuhisa et al., May 30, 1995. *
Machine-English translation of Japanese patent No. 2001-288543, Abe Masayuki et al., Oct. 19, 2001. *
Machine-English translation of Japanese patent No. 2002-105601, Hiramatsu Naoto et al., Apr. 10, 2002. *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20170253945A1 (en) * 2014-09-17 2017-09-07 Nippon Steel & Sumikin Stainless Steel Corporation Martensitic stainless steel for brake disk and method for producing said steel
US10808293B2 (en) 2015-07-15 2020-10-20 Ak Steel Properties, Inc. High formability dual phase steel

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